MR device with synthetic free layer structure

ABSTRACT

A magneto-resistive device having a large output signal as well as a high signal-to-noise ratio is described along with a process for forming it. This improved performance was accomplished by expanding the free layer into a multilayer laminate comprising at least three ferromagnetic layers separated from one another by antiparallel coupling layers. The ferromagnetic layer closest to the transition layer must include CoFeB while the furthermost layer is required to have low Hc as well as a low and negative lambda value. One possibility for the central ferromagnetic layer is NiFe but this is not mandatory.

FIELD OF THE INVENTION

The invention relates to the general field of magneto resistance (MR) with particular reference to the micro-structure of the free layer.

BACKGROUND OF THE INVENTION

Magnetic tunneling junction (MTJ) is a key component of both magnetic recording heads and magnetic random access memory (MRAM). A typical MTJ structure for a recording head or for an MRAM application is schematically illustrated in FIG. 1, as follows:

Buffer layer 11, antiferromagnetic layer (AFM) 12, an outer pinned layer, Ru, (neither shown) inner pinned layer 13 (the reference layer), tunnel barrier layer 14, free layer 15, and capping layer 16. In this structure, free layer 15 serves as the sensing layer which responds to external fields (specifically those stored in the media) while inner pinned layer 13 remains fixed and serves as reference layer. The electrical resistance through barrier (i.e. insulating) layer 14 varies with the relative orientation of the free layer moment relative to the reference layer moment thereby converting magnetic information stored in the media into electrical signals.

For effective operation as part of a magnetic recoding head, the basic requirements for TMR sensors are as following:

1) Low resistance area product (RA)

2) High magneto resistance (MR) ratio

3) A soft free layer having low magnetostriction

4) Low interlayer coupling through the barrier layer.

5) Strongly pinned reference layer.

MgO-based MTJs are promising candidates for achieving high recording density and/or high frequency application because their TMR ratio is significantly higher than those of AlOx or TiOx based MTJs. S. Yuasa et al [1] and S. S. Parkin et al. [2] demonstrated that MR ratios around 200% can be achieved at room temperature in epitaxial Fe(001)/MgO(001)/Fe(001) and with polycrystalline FeCo/MgO/(Fe₇₀Co₃₀)₈₀B₂₀ MTJs.

Yuasa et al. [3] have also reported that TMR ratios as high as 410% at room temperature can be achieved in fully epitaxial Fe(001)/Co(001)/MgO(001)/Co structures. Meanwhile, D. D. Djayaprawira et al [4] showed that MTJs of CoFeB/MgO(001)/CoFeB structure made by conventional sputtering can also have a very high MR ratio (230%) with the added advantage of greater feasibility and uniformity. For low RA applications, the MR ratio of CoFeB/Mg/MgO/CoFeB MTJs can reach 138% at RA=2.4 ohm.μm² was achieved by K. Tsunekawa et al [5] by inserting a DC-sputtered metallic Mg layer in between the bottom CoFeB and the rf-sputtered MgO, an idea initially proposed by T. Linn et al. [6] to prevent oxidation of the bottom electrode (CoFe) in a CoFe/MgO/reactive sputtering/NiFe structure. Also, Ta getter-presputtering prior to the rf-sputtered MgO layer can achieve 55% TMR with an RA of 0.4 ohm.micron² as recently reported by Y. Nagamine et al. [7]. An alternative way to form a low RA MgO barrier is to deposit two metallic Mg layers with a natural oxidation process in between as we previously proposed for the benefit of better process control and MRR uniformity. CoFeB material has been used in MgO based MTJs to achieve a magnetically soft free layer having a high MR ratio. High MR ratio and low RA has been demonstrated in MgO MTJs with CoFeB free layer. It was also demonstrated that insertion of a thin CoFe layer between MgO barrier and CoFeB facilitates getting a high MR ratio even at low annealing temperatures (ca. 300° C.). However, there remains a concern that a CoFeB free layer will have a high positive magnetostriction coefficient (lambda).

There are several possible ways to reduce lambda in a CoFeB based free layer. As shown elsewhere, lambda can be reduced by replacing CoFeB with CoB or by adjusting the CoFeB composition. However, magnetic softness deteriorated at the high annealing temperature needed to achieve a high MR ratio. To tackle this issue, a special annealing procedure was developed whereby a relatively high dR/R could be achieved while the free layer was still soft. An alternative approach for reducing lambda is to add a NiFe layer, which has negative lambda and is magnetically soft, on top of the CoFeB in the free layer. However, CoFeB/NiFe-type free layer structure is not usable because direct contact between CoFeB and NiFe causes a drastic drop in MR ratio.

H. Wang et al have proposed to use CoFe/CoFeB/Ta/NiFe as a free layer with high dR/R. In this structure, high dR/R can be achieved because the CoFeB is separated from the NiFe by a Ta insertion layer. The CoFe\CoFeB and NiFe layers are magnetically coupled through orange-peel type coupling, which tend to align magnetic moments to be parallel. However, this coupling is relatively weak and, in the case of real devices, has to compete with magnetostatic coupling from the edge of two layers which tend to align these two layers anti-parallel. As a result, magnetic noise for this kind of structure is relatively high. So although signal amplitude is high, improvement in signal-to-noise ratio is limited.

REFERENCES

-   1. S. Yuasa et al “Giant room-temperature magnetoresistance in     single-crystal Fe/MgO/Fe magnetic tunnel junctions”, Nature     Materials 3, 868-871 (2004). -   2. S. S. P. Parkin et al, “Giant tunnelling magnetoresistance at     room temperature with MgO (100) tunnel barriers”, Nature Materials     3, 862-867 (2004). -   3. S. Yuasa et al. “Giant tunneling magnetoresistance up to 410% at     room temperature in fully epitaxial Co/MgO/Co magnetic tunnel     junctions with bcc Co(001) electrodes”, Applied Physics Letters 89,     042505 (2006). -   4. D. D. Djayaprawira et al. “230% room-temperature     magnetoresistance in CoFeB/MgO/CoFeB magnetic junctions”, Applied     Physics Letters 86, 092502 (2005). -   5. K. Tsunekawa et al. “Giant tunneling magnetoresistance effect in     low-resistance CoFeB/MgO(001)/CoFeB magnetic tunnel junctions for     read-head applications” Applied Physics Letters 87, 072503 (2005). -   6. T. Linn et al., “Method of forming a barrier layer of a tunneling     magnetoresistvie sensor”, U.S. Pat. No. 0,101,978 A1 (May 27, 2004). -   7. Y. Nagamine et al. “Ultralow resistance-area product of 0.4     ohm**μm^2 and high magnetoresistance above 50% in CoFeB/MgO/CoFeB     magnetic junctions” Applied Physics Letter 89 162507 (2006). -   8. T. Zhao et al. Headway Invention Proposal HT05-045—“Low     Resistance Tunneling Magnetoresistive Sensor With Natural-Oxidized     Double MgO Barrier” -   9. H. Wang et al Headway Invention Proposal HT07-040 “TMR Sensor     with Low magnetostriction Free layer -   10. H. Wang et al Headway Invention Proposal HT07-028 “Novel Free     Layer Design for TMR/CPP Device”.     A routine search of the prior art was performed with the following     references of interest being found:

In U.S. Patent Application 2008/0117553, Carey et al. disclose a free layer comprising CoFe/spacer/NiFe/spacer/CoFe where the spacer is Cu, Au, or Ag and where a third element can be alloyed with the CoFe or NiFe. Additional discussion of this reference appears later in connection with TABLE I.

In U.S. Pat. No. 7,130,166, Gill shows a three-layer free layer where the first and third layers are CoFe/NiFe and the second layer is NiFe, but any of these layers can be NiFe, CoFe, or an CoFe/NiFe stack. The layers are separated by Ru. U.S. Pat. No. 7,141,314 (Zhang et al—Headway) teaches free layer laminates of CoFe and FeCo with spacer layers of Cu. In U.S. Pat. No. 7,149,105, Brown et al. disclose a free layer comprising NiFe and CoFeB separated by a nonmagnetic spacer such as Ru, having a thickness of 2-30 Angstroms.

U.S. Patent Application 2007/0097561 (Miyauchi et al.) shows a free layer comprising alloys of Co, Fe, Ni having a nonmagnetic layer in between while in U.S. Patent Application 2006/0291108, Sbiaa et al. describe a free layer containing a nonmagnetic spacer such as Ru, Rh, Ag, Cu.

SUMMARY OF THE INVENTION

It has been an object of at least one embodiment of the present invention to provide a magneto-resistive device having a large output signal as well as a high signal-to-noise ratio.

Another object of at least one embodiment of the present invention has been that said device be any of CIP-GMR, CPP-GMR, MTJ, and TMR devices.

Still another object of at least one embodiment of the present invention has been to provide a process for forming said magneto-resistive device.

A further object of at least one embodiment of the present invention has been for said process be fully compatible with existing processes for forming magneto-resistive devices.

These objects have been achieved by expanding the free layer into a multilayer laminate comprising at least three ferromagnetic layers separated from one another by antiparallel coupling layers, whereby the central ferromagnetic layer has a magnetization direction that is antiparallel to that of the two outer layers.

Additionally, the first of these three ferromagnetic layers, the one closest to the transition layer, must include (or consist entirely of) CoFeB while the third layer is required to have low Hc as well as a low and negative lambda value. One possibility for the central ferromagnetic layer is NiFe but this is not mandatory.

Processes for forming both the expanded free layer as well as the full device are also described.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic cross-section of a TMR stack of the prior art, including simple free layer 15.

FIG. 2 shows how free layer 15 of the prior art has been expanded into a laminate of three antiparallel coupled ferromagnetic layers.

FIG. 3 shows how the first of the ferromagnetic layers of FIG. 2 has been further expanded into a three layer laminate.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The present invention discloses a free layer structure comprising at least three magnetic layers whose magnetic moments are antiparallel coupled through Ru layers. This is illustrated in FIG. 2 which shows how the simple free layer 15 seen in FIG. 1 has been expanded to become a more complex structure. Seen in FIG. 2 are ferromagnetic layers mag1, mag2, and mag3 which have been designated as layers 21, 23, and 25 respectively. The magnetizations of layers 21 and 23 are antiparallel to each other as are those of layers 25 and 23, the required antiparallel coupling between the two pairs of layers being provided by Ru layers 22 and 24, respectively. Note that, while Ru is generally preferred, acceptable antiparallel coupling can also be achieved by using other materials such as Rh, Cu, Cr, or Ir in place of Ru. As with Ru, their thickness should be in a range of from 4-10 Å.

Mag1 can be made of single layer or combination of: CoxFe1−x(x=0˜100%), (CoxFe1−x)1−yBy (x=0˜100%, y=10˜40%) or their alloys with third or forth elements, such as Ni, Ta, Mn, Ti, W, Zr, Hf, Tb. For example, CoFeB, CoFe\CoFeB or CoFe\CoFeB\CoFe. The thickness for each layer may be 1˜40 A. Materials or structures that give higher dR/R are preferred.

Mag2 can be a single layer or a combination of: NixFe1−x (x=0˜100) CoxFe1−x(x=0˜100%) and their alloys with third or fourth elements, such as Ni, Ta, Mn, Ti, W, Zr, Hf, Tb or B. For example, CoFe, NiFe or CoFe\NiFe\CoFe. The thickness for each layer may be 1˜30 A. Materials or structures with low or negative lambda that promote strong coupling through spacers are preferred.

Mag3 can be a single layer or combination of: NixFe1−x (x=0˜100) CoxFe1−x(x=0˜100%), their alloys with third or fourth elements, such as Ni, Ta, Mn, Ti, W, Zr, Hf, Tb or B. For example, NiFe, CoFe\NiFe or CoFe\NiFe\CoFe. The thickness for each layer may be 1˜80 A. Materials or structures with negative lambda and low Hc are preferred.

The TMR barrier can be MgO, MgZnO, ZnO, Al₂O₃, TiOx, AlTiO, HfOx, ZrOx or any combination of these.

As illustrated in FIG. 3, Mag1 may be sandwiched between two layers, 31 and 33, of CoFe, each about 3 Å thick. Layer 31 enhances the MR ratio for anneal temperatures less than about 300° C. while layer 33 is for strong AP coupling through layer 22.

The characteristics required for the five main layers are summarized in TABLE I below. For comparison purposes we have also included the main features of the structures disclosed in U.S. 2008/011753, mentioned earlier in connection with our prior art search:

TABLE I 2008/0117553 PRESENT INVENTION COMMENTS MAG1 CoFe(40-60%), CoFeAl CoFeB, CoFe/CoFeB or Must include CoFeB or CoFeSi CoFe/CoFeB/CoFe, or alloy with 4^(th) element MAG2 NiFe (2-25%) CoFe, NiFe, or Not limited to NiFe CoFe/NiFe/CoFe MAG3 CoFe(40-60%), CoFeAl NiFe, CoFe/NiFe or Low Hc and negative or CoFeSi CoFe/NiFe/CoFe lambda required* APC LAYERS Cu, Au, Ag; 1-5 Å Ru, Rh, Cu, Cr, Ir; Must promote APC, 4-10 Å ruling out Au & Ag *Cannot be accomplished by CoFe (40-60%) single layer

In TABLE II below, we show data for a number of different TMR stacks having different free layer structures. Samples A and B, with free layers of CoFe3\CoFeB\Ru and CoFe3\CoFeB\CoFe\Ru respectively, have high MR ratios (up to 67% at RA 1.5) but cannot be used because of their very high positive lambda values (˜1.4E-5).

Inserting Ru\NiFex\Ru\NiFey on top allows us to significantly reduce magnetostriction while still maintaining a high MR ratio and good magnetic softness (see samples C, D, E, and F). The amount of magnetostriction and the magnetic moment can be readily tuned by adjusting the thickness of the two NiFe layers. Sample F has near zero magnetostriction, a Bs slightly higher than the reference (sample B), and an Hc of only 5.6 Oe.

In samples D and F, a thin CoFe layer has been inserted for the purpose of enhancing the coupling strength between CoFeB and NiFe layers. For example, the coupling field for CoFe3\CoFeB20\Ru8\NiFe35 is 800 Oe and which increases to 1700 Oe for CoFe3\CoFeB20\CoFe3\Ru8\NiFe35. Coupling strength could be even further improved by inserting another thin CoFe layer under the NiFe or by replacing NiFe with CoFe,

Sample G is an example of a synthetic free layer with thicker top NiFe layer and a thinner middle NiFe layer, demonstrating that Bs can be adjusted independently of total thickness and lambda.

TABLE II Sample Bs Hc ID Free Layer Structure (nW) (Oe) Lambda A CF3\CFB20\Ru 0.34 4.9 1.4E−05 B CF3\CFB20\CF3\Ru 0.37 4.5 1.4E−05 C CF3\CFB20\Ru\NF15\Ru\NF20 0.40 5.3 3.8E−06 D CF3\CFB20\CF3\Ru\NF15\Ru\NF20 0.44 5.2 3.9E−06 E CF3\CFB20\Ru\NF35\Ru\FN40 0.41 5.8 −2.3E−07 F CF3\CFB20\CF3\Ru\NF35\Ru\NF40 0.44 5.6 2.0E−08 G CF3\CFB20\CF3\Ru\NF20\Ru\NF50 0.59 4.2 −4.2E−07 MgO MTJ with CoFe\CoFeB and CoFe\CoFeB free layers. The structure of the full TMR stack was Ta\Ru\IrMn\CoFe\Ru\CoFe\MgO\FL\capping. The films were annealed at 280° C. for 5 hours in a magnetic field of 8K Oe.

Note that the free layer of the present invention may also be used in other similar MR structures (such as CIP-GMR, CPP-GMR and TMR), particularly those that need high lambda material to boost dR/R, while still retaining low free layer softness. 

What is claimed is:
 1. A process to form a free layer as part of a magneto-resistive device, comprising: depositing a barrier layer and then depositing thereon a first layer of ferromagnetic material (MAG1); depositing on MAG1 a first antiparallel coupling layer; depositing on said first antiparallel coupling layer a second layer of ferromagnetic material (MAG2); depositing on MAG2 a second antiparallel-coupling layer; depositing on said second antiparallel coupling layer a third layer of ferromagnetic material (MAG3) having a coercivity less than about 5 Oe and a negative lambda value that is more negative than about −2×10⁻⁶; and magnetizing all three ferromagnetic layers in a manner such that MAG1 and MAG3 become magnetized parallel to one another and antiparallel to MAG2.
 2. The process recited in claim 1 wherein said first and second antiparallel coupling layers are Ru.
 3. The process recited in claim 1 wherein said first and second antiparallel coupling layers are selected from the group consisting of Rh, Cu, Cr, and Ir.
 4. The process recited in claim 1 wherein the step of depositing MAG1 further comprises: depositing on said barrier layer a first layer of CoFe to a thickness in the range of from 2 to 10 Å; depositing on said first layer of CoFe a layer of CoFeB to a thickness in the range of from 10 to 40 Å; and depositing on said layer of CoFeB a second layer of CoFe to a thickness in the range of from 2 to 10 Å.
 5. The process recited in claim 1 wherein MAG2 is selected from the group consisting of CoFe, NiFe, and a CoFe/NiFe/CoFe laminate.
 6. The process recited in claim 1 wherein MAG3 is selected from the group consisting of CoFe, NiFe, and a CoFe/NiFe/CoFe laminate.
 7. The process recited in claim 1 wherein the step of magnetizing all three ferromagnetic layers in a manner such that MAG1 and MAG3 become magnetized parallel to one another and antiparallel to MAG2, is achieved without the need for a special magnetizing process.
 8. A free layer that is part of a magneto-resistive device, comprising: a first layer of ferromagnetic material (MAG1); on MAG1, a first antiparallel coupling layer; on said first antiparallel coupling layer, a second layer of ferromagnetic material (MAG2); on MAG2, a second antiparallel coupling layer; on said second antiparallel coupling layer, a third layer of ferromagnetic material (MAG3) having a coercivity less than about 5 Oe, and a negative lambda value that is more negative than about −2×10⁻⁶; and said three ferromagnetic layers being magnetized in a manner such that MAG1 and MAG3 are magnetized parallel to one another and antiparallel to MAG2, thereby stabilizing said free layer through antiparallel coupling.
 9. The free layer described in claim 8 wherein said first and second antiparallel coupling layers are Ru.
 10. The free layer described in claim 8 wherein said first and second antiparallel coupling layers are selected from the group consisting of Rh, Cu, Cr, and Ir.
 11. The free layer described in claim 8 wherein MAG1 further comprises: a first layer of CoFe having a thickness in the range of from 2 to 10 Å; on said first layer of CoFe, a layer of CoFeB having a thickness in the range of from 10 to 40 Å; and on said layer of CoFeB a second layer of CoFe having a thickness in the range of from 2 to 10 Å.
 12. The free layer described in claim 8 wherein MAG2 is selected from the group consisting of CoFe, NiFe, and a CoFe/NiFe/CoFe laminate.
 13. The free layer described in claim 8 wherein MAG3 is selected from the group consisting of CoFe, NiFe, and a CoFe/NiFe/CoFe laminate. 